Phonon-mediated superconductivity in \documentclass[12pt]{minimal} \usepackage{amsmath} \usepackage{wasysym} \usepackage{amsfonts} \usepackage{amssymb} \usepackage{amsbsy} \usepackage{mathrsfs} \usepackage{upgreek} \setlength{\oddsidemargin}{-69pt} \begin{document}$${\text{Mg}}_{{1 - x}} {\text{Mo}}_{x} {\text{B}}_{2}$$\end{document}Mg1-xMoxB2 compounds: a crystal prediction via cluster expansion and particle-swarm optimization

Investigating superconductivity represents one of the most significant phenomena in the field of condensed matter physics. Our simulations aim to elucidate the structures in the metallic state of Mg1−xMoxB2, which is essential for predicting their superconducting properties. By employing a first-principle cluster expansion and particle-swarm optimization, we have predicted the structures of Mg1−xMoxB2 ternary alloys, including Mg0.667Mo0.333B2, Mg0.5Mo0.5B2, and Mg0.333Mo0.667B2, and have determined their thermodynamically stable configurations under both atmospheric and high-pressure conditions. To investigate the potential for superconductivity in these structures, we have conducted a detailed examination of electronic properties that are pertinent to determining the superconducting state. Regarding superconducting properties, Mg0.333Mo0.667B2 exhibits superconductivity with a critical temperature (Tc) of 7.4 K at ambient pressure. These findings suggest that the theoretically predicted structures in Mg/Mo-substituted metal borides could play a significant role in synthesis and offer valuable insights into superconducting materials.


Methods
In relation to the crystallography of Mg 1−x Mo x B 2 , we conduct a comprehensive investigation of precise stoichiometries under atmospheric pressure employing a CE technique.The CE method, which combines various atomic configurations to create larger structures, may not consistently result in the lowest enthalpy.It is important to note that CE has limitations in discovering novel structures.Therefore, as a potential approach to achieve novel structures with lower enthalpy values, particularly for superconducting materials, we might consider employing the PSO algorithm within an evolutionary framework based on DFT.PSO is an advanced analytical technique that offers effective solutions for determining crystal structures under high pressure.Its precision and reliability have enabled us to accurately predict the structural characteristics of various systems, including previously unknown ones.Thanks to the capabilities of this method, significant discoveries in crystal structures have been made, especially in high-pressure conditions.Additionally, our investigation into the crystallography of Mg 1−x Mo x B 2 will delve deeper into their structural stability, taking into account the influence of SOC.Moreover, we will identify the electronic properties of the new superconducting quantum phases by examining their partial density of states (PDOS).Furthermore, it is worth noting that dynamic stability plays a crucial role in both creating and maintaining superconducting quantum phases in Mg 1−x Mo x B 2 .To summarize this work, we provide a detailed analysis of our study of superconducting properties in the following subsections.

Structural predictions
In the context of this study, we successfully predicted all configurations of Mg 1−x Mo x B 2 using the first-principles CE method initially proposed by Sanchez et al. 25 , at ambient pressure.The CE method was implemented through the MIT Ab initio Phase Stability (MAPS) code 26 , which is part of the Alloy-Theoretic Automated Toolkit (ATAT) 27 .Candidate structures, including stable and metastable ground-state configurations, were validated through first-principles calculations based on DFT, utilizing the Quantum Espresso (QE) package 28,29 .These calculations employed an energy cutoff of 80 Ry and 4000 k-point meshes.To initiate the generation of structural configurations, we explored 80 configurations for Mg 1−x Mo x B 2 .Subsequently, we investigated the derived metastable ground-state structures in Mg 1−x Mo x B 2 using the PSO approach for structural predictions.This was implemented through the Crystal structure AnaLYsis by Particle Swarm Optimization (CALYPSO) method 30,31 the Vienna ab initio simulation package (VASP) code 32 .In our search for favorable structures of Mg 1−x Mo x B 2 , we considered cell sizes of up to 4 formula units (f.u.).

Structural stability and electronic structure
For optimized calculations, the electronic band structure and density of states are computed using first-principles calculations based on DFT as implemented in the VASP 32 .We employed the generalized gradient approximation (GGA), specifically the Perdew, Burke, and Ernzerhof (PBE) exchange-correlation functional 33 , along with the conjugate gradient scheme for these computations.Details of the calculations for all structures neglected entropy contributions since they were performed at 0 K, where the formation energy suffices to confirm phase stability.The projector augmented wave (PAW) method 34 was used with valence electrons of 2s 2p 3s, 4s 4p 4d 5s, and 2s 2p, for Mg, Mo, and B atoms, respectively.The pseudocore radii for Mg, Mo, and B atoms were 1.7, Bohr 2.5 Bohr, and 1.1 Bohr, respectively, ensuring no sphere overlap under compression.Optimizing the structures involved a plane-wave basis set with a cutoff energy of 500 eV and an initial Brillouin Zone (BZ) sampling grid spacing of 2π ×0.02 Å −1 .To account for the effect of SOC with scalar-relativistic eigenfunctions, as implemented in the VASP code 32 , SOC was included in all simulations of the various phases of Mg 1−x Mo x B 2 35,36 .This is particularly relevant since Mo, being one of the heavy elements, plays a significant role in stabilizing Mg 1−x Mo x B 2 across the range of 0 < x < 1 for Mo concentration 37 .

Dynamic stability and phonon-mediated superconductivity
Phonon calculations were conducted using first-principles lattice dynamics and density-functional perturbation theory (DFPT) as implemented in the PHONOPY package 38,39 , in conjunction with the VASP code.For critical temperature superconductivity calculations, EPC and spectral function computations were also performed using DFPT 28 .A plane-wave energy cutoff of 80 Ry was utilized, and all calculations were carried out within the GGA-PBE scheme.In the context of EPC matrix element calculations for P6/mmm Mg 0.667 Mo 0.333 B 2 , R3 m Mg 0.333 Mo 0.667 B 2 , Immm Mg 0.5 Mo 0.5 B 2 , and I4 m2 Mg 0.5 Mo 0.5 B 2 , computations were performed within the first Brillouin zone (BZ) using q-meshes of 2×2×2, 2×2×4, 2×2×2, and 2×2×1, respectively.The individual EPC matrices were utilized with k-points meshes of 16×16×24, 12×12×12, 24×24×24, and 12×12×1.It is worth noting that the Eliashberg spectral function depended on a dense k-points mesh, encompassing all k and k+q grid points, which covered the q-points mesh, as implemented in the Quantum Espresso code 29 .These conditions for q-points and the calculated spectral function align with findings from previous theoretical studies 40,41 .The Allen-Dynes (AD) equation 42 was employed with an effective Coulomb pseudopotential parameter, µ * = 0.10.

Results and discussion
To explore various stoichiometries involving Mg/Mo-substituted metal borides, we employed the CE method.Thermodynamic stability of the novel Mg 1−x Mo x B 2 structures is presented under ambient conditions, where 0 ≤ x ≤ 1.The formation energy at ambient pressure is depicted by a convex hull in Fig. 1.Predicted structures refer to those for which energies have not yet been calculated using DFT, while known structures have their energies confirmed by DFT.Furthermore, known ground states refers to the ground state energies that have been verified through DFT.To select configurations accurately, we considered a parity plot consisting of 80 chosen configurations, which achieved a satisfactory level of accuracy with a cross-validation (CV) score 26 amounting to 0.12 eV/site.In essence, the CE method's solution enabled us to explore novel compositions within Mg 1−x Mo x B 2 .Our primary structural prediction results unveiled ground-state structures.The current structural predictions rely on these ground-state structures, determined through the calculation of the formation energy, which is obtained as Figure 1.Formation energy at ambient pressure for the Mg 1−x Mo x B 2 system, covering a range of 0 ≤ x ≤ 1.The term "predicted" denotes structures for which energy calculations have not been conducted via DFT, "known str" signifies structures for which DFT-based energy calculations have been performed, and "known gs" indicates ground state energies that have been validated through DFT calculations.
Vol:.( 1234567890 www.nature.com/scientificreports/ it should be mentioned that MoB 2 , initially adopted from the MgB 2 -type with a hexagonal structure (symmetry: P6/mmm), might not be the ground state structure.As a result, corresponding formation energies are normalized by the rhombohedral β -MoB 2 structure, as shown in the results presented in Fig. 2. According to Fig. 2, the relatively most stable structures along the convex hull are Mg 0.667 Mo 0.333 B 2 , and Mg 0.5 Mo 0.5 B 2 , and Mg 0.333 Mo 0.667 B 2 .These candidate structures underwent structural relaxation calculations based on DFT without SOC at zero pressure.However, the present results indicate that Mg 0.333 Mo 0.667 B 2 experiences slight destabilization at ambient pressure when SOC is considered.The overall impact of SOC on x = 0.667 is not very pronounced.When Mg 0.667 Mo 0.333 B 2 and Mg 0.333 Mo 0.667 B 2 are subjected to computational compression, both structures remain thermodynamically stable at a pressure of 25 GPa, as confirmed by calculations performed both with and without SOC.However, notable differences emerge in the case of Mg 0.5 Mo 0.5 B 2 .It suggests that Mg 0.5 Mo 0.5 B 2 is thermodynamically metastable at the pressure of 25 GPa, as indicated by its position above the convex hull between Mg 0.667 Mo 0.333 B 2 and Mg 0.333 Mo 0.667 B 2 in Fig. 2. At this stage, one possible approach to achieve a stable structure in Mg 0.5 Mo 0.5 B 2 is to consider predicting its crystallography using the PSO algorithm within an evolutionary framework based on DFT.The PSO method is a powerful tool for high-pressure systems and has effectively predicted stable ground-state structures.Consequently, we can compare the results from both methods (CE and PSO) using formation enthalpy as a basis.
As discussed previously regarding the calculations involving SOC, our results indicate that the influence of SOC on the structures of Mg 1−x Mo x B 2 ternary alloys, including Mg 0.667 Mo 0.333 B 2 , Mg 0.5 Mo 0.5 B 2 , and Mg 0.333 Mo 0.667 , especially at high pressure, is not significant.Therefore, for all considered structures, our simulations are conducted without including SOC.Now, let's focus on the stable structure of Mg 0.5 Mo 0.5 B 2 at the pressure of 25 GPa, which is predicted to have a tetragonal structure with the space group I 4m2 .With this result, we constructed the convex hull, displaying the formation enthalpy.Herein, we observed that the I 4m2 structure of Mg 0.5 Mo 0.5 B 2 is thermodynamically more favorable than the Immm structure of Mg 0.5 Mo 0.5 B 2 by approximately -0.013 eV/atom.The open circle represents the CE calculation, while the solid circle represents the PSO calculation, as shown in Fig. 2. Furthermore, we found that cluster expansion is generally a reliable method for determining stoichiometry; however, in this particular case, it may not have yielded the lowest enthalpy 43 .Utilizing the PSO technique, a thorough exploration of atomic configurations aims to pinpoint the one with the lowest enthalpy, symbolizing heightened stability and favorable thermodynamics.Consequently, we accentuate the significance of the I 4m2 Mg 0.5 Mo 0.5 B 2 structure, shedding light on its potential applications.This particular structure, with its distinction as the lowest-enthalpy configuration, guarantees stability even under conditions of compression.The utmost significance of its lowest enthalpy becomes evident when considering the requirement for resilient structures that can endure compression.Considering the paramount importance of stability in the I 4m2 structure of Mg 0.5 Mo 0.5 B 2 , it becomes particularly valuable as it can maintain its form even when subjected to high levels of compression.Demonstrably, the I 4m2 Mg 0.5 Mo 0.5 B 2 structure resists decomposition into MgB 2 and MoB 2 , even under extreme pressures beyond 25 GPa up to 50 GPa, as depicted in Fig. 3.These findings are substantiated by thermodynamic calculations, with further discussions on dynamical stability to be addressed in subsequent phonon calculations.Figure 4 visually represents the P6/mmm Mg 0.667 Mo 0.333 B 2 , the R 3m Mg 0.333 Mo 0.6667 B 2 , the Immm Mg 0.5 Mo 0.5 B 2 , and the I 4m2 Mg 0.5 Mo 0.5 B 2 .Detailed structural parameters for these configurations are provided in Table 1.
At this juncture, it is noteworthy to reiterate that, under ambient pressure conditions, the R 3m Mg 0.333 Mo 0.667 B 2 , P6/mmm Mg 0.667 Mo 0.333 B 2 , and Immm Mg 0.5 Mo 0.5 B 2 structures all exhibit negative formation relative to MgB 2 and MoB 2 .However, it's crucial to emphasize that this alone does not guarantee structural stability.To address this concern, we have conducted an investigation into their dynamical stability.Consequently, we found that the P6/mmm Mg 0.667 Mo 0.333 B 2 structure is dynamically unstable due to the presence of imaginary frequencies around high symmetry points (A, H, and L), as illustrated in Fig 5(a).This implies that the P6/mmm Mg 0.667 Mo 0.333 B 2 configuration is indeed a metastable structure.However, it is important to acknowledge that the possibility of synthesis remains, as approximately 20% of materials have been successfully obtained from metastable structures 44,45 .Furthermore, it is worth noting that the results presented here are based on calculations within the harmonic approximation.Given that this structure is already stable in the thermodynamic sense, it suggests the potential for achieving an anharmonic state 46 .Additionally, we emphasize the need for further investigation into the P6/mmm Mg 0.667 Mo 0.333 B 2 structure by considering the effects of thermally excited lattice  www.nature.com/scientificreports/dynamics on its stability.For example, the theoretical explanation of a simple cubic structure in calcium [47][48][49] is well corroborated by experimental observation 50 .We have identified two dynamically stable structures, namely, the R where N F , ǫ k , and g ν kk ′ denote the DOS at E F , the e-ph matrix element between two electronic states of wave vector k and k ′ , the energy eigenvalue of the Kohn-Sham state with respect to the Fermi level, the electronphonon matrix element for the scattering between the electronic states k and k ′ via a phonon with wave vector of q = k ′ − k , while ω qν indicate the phonon frequencies.Herein, it ought to be noted that the DOS is associ- ated with Eliashberg spectral function in Eq. 2. The substantial total DOS at the Fermi level observed here can be primarily attributed to the magnitude of the electron-phonon matrix element.A comprehensive theoretical explanation of this phenomenon can be found in Ref 52 , shedding light on why the EPC varies in magnitude among these borides, thereby influencing the enhancement of their T c .As a result, the estimated DOS values at the Fermi level for R 3m Mg 0.333 Mo 0.667 B 2 , Immm Mg 0.5 Mo 0.5 B 2 and I 4m2 Mg 0.5 Mo 0.5 B 2 is estimated to be 0.138, 0.03, and 0.04 eV/state/atom, respectively.To elucidate the influence of the DOS at the Fermi level on the calculated superconducting properties and T c enhancement, we will delve into this aspect in detail below.
Regarding the Eliashberg spectral function ( α 2 F(ω )) as depicted in Fig. 7, we initially examine the outcome for the P6/mmm MgB 2 at ambient condition.The α 2 F(ω ) profile of the P6/mmm MgB 2 theoretically encom- passes contributions from both acoustic and optical modes.Notably, α 2 F(ω ) value is particularly pronounced in the optical phonon mode, resulting in a significant integration of , as illustrated in Fig. 7(a).We observed that the P6/mmm MgB 2 has a value of 0.80.Now, let's shift our focus to the stable structures, namely, the R 3m Mg 0.333 Mo 0.667 B 2 and the Immm Mg 0.5 Mo 0.5 B 2 at ambient condition.Our findings indicate that α 2 F(ω ) encompasses contributions spanning from acoustic to optical modes, which are illustrated in Figs.7(b) and 7(c).Similarly, the I 4m2 Mg 0.5 Mo 0.5 B 2 structure also demonstrates α 2 F(ω ) contributions spanning the acoustic to optical modes at a pressure of 50 GPa, as depicted in Fig. 7(d).Subsequently, we theoretically derived the EPC constant, denoted as , by using the Eq. ( 3).This can be determined by integrating α 2 F(ω ).Broadly speaking, the solution exhibits a sharp increase in the low-frequency phonon mode, followed by a gradual increase in the medium-frequency phonon mode.It then experiences a slight rise up to the highest phonon frequency, thus showcasing the overall integrated .Consequently, the integrated of R 3m Mg 0.333 Mo 0.667 B 2 , Immm Mg 0.5 Mo 0.5 B 2 , and the I 4 m2 Mg 0.5 Mo 0.5 B 2 is 0.62, 0.32, and 0.36, respectively.As previously mentioned, the DOS significantly influences the .Notably, the DOS of R 3m Mg 0.333 Mo 0.667 B 2 is predominantly concentrated at the Fermi level, which is directly reflected in the value.This observation clarifies why the is notably high in this case.Moreover, it is intriguing to note that the EPC constant's magnitude is governed by the DOS.This raises the possibility that the Mo concentration plays a crucial role, given its contribution at the Fermi level.This factor may hold importance in understanding the superconducting mechanism.
To assess the T c , we employed the AD equation with µ * = 0.10.Initially, we examined the cd T c of the P6/ mmm MgB 2 , and found it to exhibit superconductivity with a T c of 34 K.This result aligns well with experimental observations 1 .Subsequently, we determined the T c of the R 3m Mg 0.333 Mo 0.667 B 2 and the Immm Mg 0.5 Mo 0.5 B 2 .Our comprehensive analysis also indicates superconductivity in these compounds, with the T c values of 7.4 K and 0.43 K, respectively, at ambient pressure.Notably, our study reveals that the T c of the R 3m Mg 0.333 Mo 0.667 B 2 and the Immm Mg 0.5 Mo 0.5 B 2 are relatively low compared to the T c of the P6/mmm MgB 2 .The underlying reason for this discrepancy can be attributed to our critical analysis of the the EPC and ω log values, primarily influenced by the presence of Mo atoms.This suggests that the presence of Mo may be one of the factors limiting the increase in T c In addition to µ * = 0.10, these findings may hold relevance even when the µ * = 0.13 is not uni- versally applicable to all simple metals 53 , as it is primarily suited for transition metals.To some extent, however, it is reasonable to anticipate that adopting µ * = 0.13 in theoretical predictions might result in an enhancement of T c .At this juncture, particular attention should be directed towards the R 3m Mg 0.333 Mo 0.667 B 2 due to its substantially higher T c compared to the Immm Mg 0.5 Mo 0.5 B 2 .Specifically, the R 3m Mg 0.333 Mo 0.667 B 2 exhibits superconductivity with a T c of 5.34 K and it is noteworthy that its T c decreases when µ * = 0.13 is employed.It is important to highlight that the T c values observed in Mg 0.333 Mo 0.667 B 2 and Mg 0.5 Mo 0.5 B 2 are significantly lower than that of MgB 2 , where µ * = 0.10 is used 10 .As indicated by previous theoretical findings 10 , the high DOS of boron at the Fermi level plays a pivotal role in achieving high-T c in MgB 2 .In contrast, within our system, it appears that the DOS of boron in Mg 0.333 Mo 0.667 B 2 and Mg 0.5 Mo 0.5 B 2 may not be sufficiently high in comparison to MgB 2 , thereby limiting their T c potential.However, it becomes intriguing to further investigate the T c behavior of these compounds under compression.Beyond ambient pressure, up to 25 GPa, we have observed that the R 3m Mg 0.333 Mo 0.667 B 2 exhibits superconductivity with a T c of 5.3 K, while, the T c of the I 4m2 Mg 0.5 Mo 0.5 B 2 reached 1.12 K at 25 K. Beyond 25 GPa, there is a general trend of decreasing T c with increasing pres- sure.A summary of the main results is presented in Table 2. Therefore, considering the impact of compression, it is reasonable to speculate that these structures have the potential for superconductivity up to at least 50 GPa.The primary effect of compression suggests that increasing pressure may not be conducive to maintaining the superconducting state in these structures, as there is a clear trend toward transitioning from a superconducting state to a normal metallic state under compression.As previously mentioned in experimental findings 23 , despite the discrepancy between experimental observations and our theoretical explanations, particularly regarding the evolution of T c at ambient conditions, one aspect related to the concentration of Mo is noteworthy.It is evident that the specific crystal structure plays a critical role in this context.This implies that the evolution of T c may indeed be influenced by the concentration of Mo, especially when the Mo atom's placement aligns with the (2) lattice site.Consequently, this could explain why a reduced T c was observed in experimental studies.While this analysis provides a straightforward starting point for understanding the relationship, it also poses a challenge to the assumptions made.Therefore, we propose that the influence of Mo concentration on MgB 2 warrants further experimental investigations.Regarding the bonding environment of the R 3 m Mg 0.333 Mo 0.667 B 2 , the Immm Mg 0.5 Mo 0.5 B 2 , and the I 4m2 Mg 0.5 Mo 0.5 B 2 , we have explored their electronic properties using the electron localization function (ELF) method. 54.The ELF provides insights into the distribution of electrons within crystals relative to a uniform electron gas of the same density, with ELF values ranging between 0 and 1, indicating the tendency of electron pairing.ELF values are always positive.To begin, let's examine the bonding environment of R 3m Mg 0.333 Mo 0.667 B 2 .We illustrate this environment in the (110) atomic plane, where the ELF reveals that electrons tend to accumulate more favorably between Mo and B atoms than between Mg and B atoms, as depicted in Fig. 8(a 17,[55][56][57][58][59][60] .Considering the bonding environment's influence on the system, the electron contributions between Mo and B atoms appear to be significantly connected with the observed T c .In our research, we propose that the emergence of superconductivity could potentially be observed in new metallic phases present in the Mg 1−x Mo x B 2 system, under both ambient and high-pressure conditions.If this hypothesis holds true, it would be worthwhile to explore further through analyses using energy dispersive X-ray spectroscopy (EDS) and X-ray photoelectron spectroscopy (XPS) to gain insights into the underlying chemical bonding 61 .

Conclusion
In summary, we present the discovery of novel metallic phases within the Mg 1−x Mo x B 2 system, utilizing a combination of first-principles cluster expansion and particle swarm optimization techniques.Among the structures located along the convex hull, Mg 0.667 Mo 0.333 B 2 , Mg 0.5 Mo 0.5 B 2 , and Mg 0.333 Mo 0.667 B 2 , exhibit the lowest enthalpy, and they remain stable at ambient pressure.Remarkably, these structures maintain their structural stability even under high pressures, extending up to at least 50 GPa.An analysis of the density of states reveals that the electronic states of Mg 0.333 Mo 0.667 B 2 near the Fermi level exhibit a high sensitivity to electron-phonon coupling when compared to Mg 0.5 Mo 0.5 B 2 .Consequently, Mg 0.333 Mo 0.667 B 2 demonstrates a considerably high T c of 7.4 K, even at ambient pressure.These findings highlight the significance of molybdenum substitution in magnesium diboride as it pertains to achieving high T c superconductors.We anticipate that our results will encourage further experimental investigations in this category of superconducting materials.
in this equation, E f represents the formation energy, E[Mg 1−x Mo x B 2 ] denotes the total energy of Mg 1-x Mo x B 2 with concentration in the range 0 < x < 1, E[MgB 2 ] is the total energy of MgB 2 with a hexagonal structure, E[MoB 2 ] represents the total energy of MoB 2 with a rhombohedral β -MoB 2 structure.It is important to note that MgB 2 and MoB 2 in Eq. (1) correspond to the hexagonal structure and the rhombohedral β-MoB 2 structure, respectively.The results indicate that Mg 0.667 Mo 0.333 B 2 , Mg 0.5 Mo 0.5 B 2 , and Mg 0.333 Mo 0.667 B 2 are energetically stable.This clearly confirms their stability against decomposition into MgB 2 and MoB 2 at ambient pressure.However, (1) 13:20295 | https://doi.org/10.1038/s41598-023-44632-3

Figure 2 .
Figure 2. Formation enthalpy at 0 K for the Mg 1−x Mo x B 2 system, ranging from 0 ≤ x ≤ 1. Circles and squares represent calculations at pressures of 0 GPa and 25 GPa.Filled circles and squares indicate stable structures, while open circles and squares represent metastable ones.Panels (a) and (b) correspond to calculations without and with spin-orbit coupling (SOC), respectively.

Figure 3 .
Figure 3. Formation enthalpy at temperature of 0 K of Mg 1−x Mo x B 2 system, spanning from 0 ≤ x ≤ 1. Circles, squares, and triangles denote calculations at pressures of 0 GPa, 25 GPa, and 50 GPa, respectively.Filled circles and squares represent stable structures.

3 mFigure 6 .
Figure 6.Density of states under different pressures: (a) the P6/mmm MgB 2 at ambient pressure, (b) the R 3m Mg 0.333 Mo 0.667 B 2 at ambient pressure, (c) the Immm Mg 0.5 Mo 0.5 B 2 at ambient pressure, and (d) the I 4m2 Mg 0.5 Mo 0.5 B 2 at the pressure of 25 GPa.

Figure 7 .
Figure 7.The spectral function as a function of frequency: (a) the P6/mmm MgB 2 at ambient pressure, (b) the R 3m Mg 0.333 Mo 0.667 B 2 at ambient pressure, (c) the Immm Mg 0.5 Mo 0.5 B 2 at ambient pressure, and (d) the I 4m2 Mg 0.5 Mo 0.5 B 2 at the pressure of 25 GPa.
).In the Immm Mg 0.5 Mo 0.5 B 2 , the ELF analysis reveals that electrons tend to accumulate more favorably between Mo and B atoms than between Mg and B atoms in both the (011) and (100) atomic planes, as depicted in Fig 8(b).Similarly, in the I 4m2 Mg 0.5 Mo 0.5 B 2 , the ELF analysis in the (100) atomic plane indicates that electrons prefer- entially accumulate between Mo and B atoms, while they do not favorably accumulate between Mg and B atoms, as shown in the Fig 8(c).Furthermore, a strong covalent bond is indicated by the significant electron accumulation between B and B atoms.It is noteworthy that the bonding environment of Mo-B, Mg-B, and B-B exhibits characteristics of both ionic and covalent bonds

Figure 8 .
Figure 8.The electron localization function: (a) R 3m Mg 0.333 Mo 0.667 B 2 at ambient pressure, (b) the Immm Mg 0.5 Mo 0.5 B 2 at ambient pressure, and (c) the I 4m2 Mg 0.5 Mo 0.5 B 2 at the pressure of 50 GPa.

Table 2 .
Electron-phonon interaction and logarithmic averages of phonon frequencies.The T c s are calculated using the isotropic Eliashberg equations.A µ * = 0.10 is used. 1 This work. 2 Reference 1 .